CN109423577A - A kind of high-strength multi-phase Steels uncoated tinplate base and its manufacturing method - Google Patents

A kind of high-strength multi-phase Steels uncoated tinplate base and its manufacturing method Download PDF

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CN109423577A
CN109423577A CN201710761690.6A CN201710761690A CN109423577A CN 109423577 A CN109423577 A CN 109423577A CN 201710761690 A CN201710761690 A CN 201710761690A CN 109423577 A CN109423577 A CN 109423577A
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phase steels
uncoated tinplate
martensite
tinplate base
strength multi
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CN109423577B (en
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连福亮
梁高飞
陈红星
班必俊
李秀军
徐刚
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to CN201710761690.6A priority Critical patent/CN109423577B/en
Priority to RU2020120647A priority patent/RU2771643C2/en
Priority to PCT/CN2018/102619 priority patent/WO2019042268A1/en
Priority to US16/642,433 priority patent/US11891674B2/en
Priority to EP18850495.5A priority patent/EP3705594B1/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/003—Cementite
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

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Abstract

A kind of high-strength multi-phase Steels uncoated tinplate base and its manufacturing method, the ingredient percent of the multi-phase Steels uncoated tinplate base are as follows: C 0.081~0.14%, Mn 0.2~0.8%, Al 0.01~0.09%, P 0.01~0.03%, N 0.002~0.015% also contains B 0.001~0.005%, Cr 0.005~0.05%, Ti 0.001~0.1%, Nb 0.001~0.2%, Cu 0.005~0.03%, it is one or more kinds of in Mo 0.001~0.008%, remaining Fe and inevitable impurity；And meet: 0.21%≤Mn+1.3Cr+3.2Mo+0.5Cu≤0.91%.The uncoated tinplate base tissue includes ferrite crystal grain, pearlite, martensite and cementite particle, wherein the total volume fraction of pearlite, martensite and cementite particle is 5~20%, and Martensite Volume Fraction is 1~5%, carbon solid solution capacity >=0.07% in martensite.The uncoated tinplate base has high-intensitive and preferable elongation percentage, can be used for producing the three-piece can body more demanding to intensity and elongation percentage, tank bottom, easy-open end, unscrewing lid etc..

Description

A kind of high-strength multi-phase Steels uncoated tinplate base and its manufacturing method
Technical field
The present invention relates to a kind of high-strength multi-phase Steels uncoated tinplate base and its manufacturing methods.
Background technique
Tin plate is a kind of tin plating obtained packaging material of surface of steel plate, tin plate in combination with steel plate high intensity and The high corrosion-resistant feature of tin layers and the outer packing for being widely used in food, beverage, chemical industry etc., are such as used for various two panels, three pieces Tank, bucket, Yi Kai, unscrewing lid etc..In recent years, based on people to energy-saving and emission-reduction, the continuous requirement of this consumption reduction, the thickness of tin plate drop Just constantly it is thinned, such as common beverage can with DI material thickness has been thinned to 0.21 from 0.28~0.29mm twenty years ago~ 0.22mm, it is tin plating that the thickness of easy-open end tin plate from the 0.25mm or so of once cold rolling tin plate has been thinned to secondary cold-rolling 0.18mm of plate or so.To guarantee the normal use after material is thinned, requirement of the people to tin plate intensity is also higher and higher.
Patent WO2008/102006A1 discloses a kind of production method of high-strength uncoated tinplate base, is mentioned by low-temperature annealing High armor plate strength guarantees steel plate elongation percentage by selecting the steel grades (5~40ppm of phosphorus content) of Ultra-low carbon, can finally give birth to Produce a series of thin uncoated tinplate bases of yield strength 500MPa or more.But the strip is ultra-low-carbon steel, and process for making needs additional vacuum Decarburization, steel-making cost are high.
United States Patent (USP) US20150010779A1 discloses a kind of tensile strength at least 500MPa, and fracture elongation is greater than 5% Uncoated tinplate base production method.The steel plate alloying component are as follows: C≤0.1%, N≤0.02%, Mn≤0.5%, Si≤ 0.04%, Al≤0.1%, Cr≤0.1%, P≤0.03%, Cu≤0.1%, Ni≤0.1%, Sn≤0.04%, Mo≤ 0.04%, V≤0.04%, Ti≤0.05%, Nb≤0.05%, B≤0.005% are quickly added by carrying out continuous annealing section Thermal velocity (75K/s is preferentially greater than 100K/s) is heated to 700 DEG C or more, by the short time heat preservation of 1~2s and cooling velocity 100~1200K/s, can get tensile strength at least 500MPa, and fracture elongation is greater than 5% uncoated tinplate base.The technology is continuous Annealing section require quickly carry out, heating speed and cooling velocity are all very high, this just to equipment, operation control accuracy requirement very Height is difficult to realize extensive stable industrial production.
Chinese patent CN101999009A discloses a kind of above high strength container uncoated tinplate base of tensile strength 500MPa Production method, steel grades are as follows: C:0.01~0.05%, Si:0.04% or less, Mn:0.1~1.2%, S:0.10% with Under, Al:0.001~0.100%, N:0.10% or less, P:0.0020~0.100%, surplus is by Fe and inevitable impurity It constitutes.The critical process of this method is under the rolling of secondary cold-rolling section that rate is 20~50%.This method obtain band hardness of steel it is high but Secondary cold-rolling rolls lower rate height simultaneously, causes strip elongation percentage low, is not suitable for the purposes that there is certain formability to require.
Summary of the invention
The purpose of the present invention is to provide a kind of high-strength multi-phase Steels uncoated tinplate base and its manufacturing method, property after steel plate baking Lower rate can be rolled with its secondary cold-rolling production section meet following relationship: yield strength Rp0.2 >=(400+12 × DCR) MPa, elongation percentage A >=(25-1.2 × DCR) %, 5%≤DCR≤18%, the uncoated tinplate base have high-intensitive and preferable elongation percentage, can be used for producing The three-piece can body more demanding to intensity and elongation percentage, tank bottom, easy-open end, unscrewing lid etc..
In order to achieve the above objectives, the technical scheme is that
A kind of high-strength multi-phase Steels uncoated tinplate base, chemical component mass percent are as follows: C:0.081~0.14%, Mn:0.2 ~0.8%, Al:0.01~0.09%, P:0.01~0.03%, N:0.002~0.015%, also containing B:0.001~ 0.005%, Cr:0.005~0.05%, Ti:0.001~0.1%, Nb:0.001~0.2%, Cu:0.005~0.03%, Mo: One or more kinds of in 0.001~0.008%, surplus is Fe and inevitable impurity；And following relationship need to be met simultaneously: 0.21%≤Mn+1.3Cr+3.2Mo+0.5Cu≤0.91%.
Further, the tissue of the high-strength multi-phase Steels uncoated tinplate base is by ferrite crystal grain, pearlite, martensite and cementite Particle composition.
Preferably, ferrite grain size≤7 μm in the tissue of the high-strength multi-phase Steels uncoated tinplate base.
Preferably, tissue medium pearlite+martensite+cementite particle volume of the high-strength multi-phase Steels uncoated tinplate base point Number is 5~20%.
Preferably, Martensite Volume Fraction is 1~5% in the tissue of the high-strength multi-phase Steels uncoated tinplate base.
Preferably, carbon solid solution capacity >=0.07% in the martensite of the high-strength multi-phase Steels uncoated tinplate base tissue.
Further, after the high-strength multi-phase Steels uncoated tinplate base baking, yield strength Rp0.2 >=(400+12 × DCR) MPa, Elongation percentage A >=(25-1.2 × DCR) %, wherein DCR is that secondary cold-rolling rolls lower rate, 5%≤DCR≤18%.
In the ingredient design of high-strength multi-phase Steels uncoated tinplate base of the present invention:
C:C element is main intensified element in the material, the present invention in C it is main to the schedule of reinforcement of strip there are two: First is that the solid solution by carbon in martensitic structure is strengthened, the other is C is analysed in the form of pearlite synusia or cementite particle Strengthened out.To guarantee strip strengthening effect, the C of addition >=0.081% is needed in steel plate.C content is excessively high to be easy annealed Be precipitated on Cheng Zhongcong ferrite grain boundaries, to reduce the plasticity of steel plate, and to the final processing performance of product, welding performance, respectively to The same sex especially also adversely affects performance after material Baking out.Therefore, C content is controlled 0.081 in steel of the present invention ~0.14%.
Main function is close with C element in the present invention for Mn:Mn element, can be further improved steel plate by the solid solution of Mn Intensity.Furthermore Mn element forms MnS with sulphur in steel, eliminates the red brittleness problem of steel caused by S, improves the hot-working character of steel. But Mn too high levels can cause in block apparent banded structure distribution in Mn segregation and hot rolled plate, to final thin plate Pressworkability is unfavorable, especially when steel band local deformation is larger (riveted forming process when such as production easy-open end), Mn's Segregation is easy to cause Local Cracking.Therefore, Mn content is controlled 0.2~0.8% in steel of the present invention.
Al:Al element mainly plays deoxidation in steel, while can refine crystal grain, and N element and Al form AlN in steel It is precipitated, eliminates influence of the N element to strip Baking out timeliness.Al excessive addition is easily reduced the Castability of slab.Cause This, the Al content that the present invention is applicable in steel is controlled 0.01~0.09%.
P:P element is also solution strengthening element, can improve the intensity of steel, but excessive P increases the cold brittleness and modeling of steel plate Property, reduce the cold-bending property and welding performance of steel.Therefore, P content is controlled 0.01~0.03% in the present invention.
The solid solution of N:N element can greatly improve the intensity of steel, but the too high baking-aging resistant that will lead to strip of N content simultaneously Performance is poor, and isotropism also will receive influence, and therefore, N content control is 0.002~0.015% in sheet metal of the present invention.
For acquisition room temperature martensitic phase tissue, need to guarantee to generate certain austenite phase during steel plate annealing, Gu Mn, The proportion of the alloying components such as Cr, Mo, Cu is most important.The proportion that these alloying components are controlled in the present invention is 0.21%≤Mn+ 1.3Cr+3.2Mo+0.5Cu≤0.91%.When the value is lower than 0.21%, martensite content is too low, and plate property is insufficient；It is higher than When 0.91%, to guarantee that steel plate strength and ductility product, secondary cold-rolling process window reduce, manufacture difficulty is larger.In addition, the addition of B element The baking-aging resistant performance of thin steel strip can be improved, the loss of elongation percentage after steel plate baking is reduced；Ti, Nb element is added, influences to move back Austenite grain size when fiery then influences room temperature multi-phase Steels tissue morphology and mechanical property.It therefore, can be according in practical application Specific requirement to intensity after baking-aging and elongation percentage carries out above-mentioned tune to constituent contents such as Mn, Cr, Mo, Cu, B, Ti, Nb Control.
The final tissue signature of high-strength multi-phase Steels uncoated tinplate base of the present invention requires as follows: organize by ferrite crystal grain, Pearlite, martensite and cementite particle composition.Wherein: ferrite grain size≤7 μm in vertical rolling direction；Band structure of steel Medium pearlite, martensite and cementite particle account for the 5~20% of tissue volume score；Martensite accounts for tissue volume in band structure of steel Score is 1~5%；Carbon solid solution capacity >=0.07% in strip martensite.
Ferrite is the most typically tissue of general cold steel in steel plate tissue, and uncoated tinplate base of the present invention controls ferrite crystal grain Size≤7 μm ensure that the intensity of ferrite matrix by refined crystalline strengthening.But it only can not be reached by ferritic crystal grain refinement To high-intensitive requirement, therefore in uncoated tinplate base tissue of the present invention, there is also pearlite, martensite, three kinds of cementite particle reinforcings Phase, wherein pearlite and martensite are main hardening constituents, and the austenite cooling generated by annealing heating is transformed.Pearlite It is made of ferrite item and cementite item, is generally generated under higher temperature while cooling；Martensite be solid solution ferrite, one As generate under lower temperature while cooling, it is maximum to the invigoration effect of steel.
For the invigoration effect for guaranteeing pearlite and martensite, the present invention claims tissue medium pearlite, martensite and cementites Particle accounts for 5% of total volume fraction or more.Pearlite and martensitic plastic are poor, and excessive pearlite and martensite will lead to strip The elongation percentage of steel reduces, therefore, high-strength multi-phase Steels uncoated tinplate base medium pearlite of the present invention, martensite and cementite particle Total volume fraction is below 20%.
In addition, martensite is required 1% or more, to prevent in band structure of steel of the invention for the reinforcing for guaranteeing strip Adverse effect of more martensites to strip plasticity, martensitic structure control below 5%；Meanwhile to guarantee martensite to strip Strengthening effect, in strip of the present invention in martensite carbon solid solution capacity 0.07% or more.
The manufacturing method of high-strength multi-phase Steels uncoated tinplate base of the present invention, the ingredient percent of the uncoated tinplate base are as follows: C:0.081~0.14%, Mn:0.2~0.8%, Al:0.01~0.09%, P:0.01~0.03%, N:0.002~ 0.015%, also contain B:0.001~0.005%, Cr:0.005~0.05%, Ti:0.001~0.1%, Nb:0.001~ 0.2%, Cu:0.005~0.03%, one or more kinds of in Mo:0.001~0.008%, remaining is Fe and inevitable miscellaneous Matter；And following relationship: 0.21%≤Mn+1.3Cr+3.2Mo+0.5Cu≤0.91% need to be met simultaneously；The uncoated tinplate base successively passes through Continuous annealing, secondary cold-rolling, wherein continuous annealing section temperature T are as follows: (727-100 × C-30 × Mn-1000 × N) DEG C≤T≤ 800 DEG C, soaking time 30s~50s, 50~90 DEG C/s of cooling velocity in 250 DEG C of temperatures above sections；Secondary cold-rolling rolls lower rate DCR:5%≤DCR≤18%.
Further, production stage of the uncoated tinplate base before continuous annealing are as follows: smelting, hot rolling, pickling, once cold rolling.
For the generation of final the tissue medium pearlite, martensite of guarantee multi-phase Steels uncoated tinplate base, it is necessary to control strip annealing Bringing-up section temperature is higher than austenite transition temperature, and essential element C, Mn, N will affect austenitizing temperature, therefore, this hair in steel The continuous annealing temperature T of oolemma steel >=(727-100 × C-30 × Mn-1000 × N) DEG C；But excessively high annealing temperature will lead to band Crystalline grain of steel is sharply grown up, to reduce band hardness of steel, therefore annealing temperature T≤800 DEG C.Consolidate the continuous annealing section control of invention Annealing temperature T is (727-100 × C-30 × Mn-1000 × N) DEG C≤T≤800 DEG C.
To guarantee that austenitizing is complete in strip annealing process, it is desirable that soaking time >=30s；Soaking time of annealing is longer, It grows up with crystalline grain of steel more serious, therefore is guaranteeing strip austenitizing simultaneously, soaking time≤50s.Therefore, the present invention is continuous It is 30s~50s that annealing section, which controls soaking time,.
In the present invention, annealing speed determines that pearlite, the amount of martensite, pearlite silver spacing, C's consolidates in martensite Molten amount.For the optimal institutional framework for guaranteeing strip, it is desirable that cooling velocity >=50 DEG C/s in 250 DEG C of temperatures above sections, cooling speed Spend it is low will lead to the more complete and martensite-free formation of perlitic transformation, and the pearlite silver spacing obtained is coarse, strip Strength reduction；Cooling velocity≤90 DEG C/s in 250 DEG C of temperatures above sections is also required, cooling velocity is excessively high, can inhibit pearlite Phase transformation, although improving band hardness of steel, loses strip elongation percentage so that martensite volume is excessive in tissue significantly.Therefore, of the invention Continuous annealing section 250 DEG C of temperatures above range restraint cooling velocities be 50~90 DEG C/s.
High-strength multi-phase Steels uncoated tinplate base of the present invention carries out secondary cold-rolling, the main work of secondary cold-rolling after continuous annealing With being strip to be further thinned, and further increase band hardness of steel, but strip elongation percentage can be reduced simultaneously, therefore, the present invention It is required that secondary cold-rolling rolls lower rate DCR≤18%.
Based on chemical component described above, tissue and manufacturing method, high-strength multi-phase Steels uncoated tinplate base provided by the present invention After 150~300 DEG C, the baking of 15~60min, yield strength Rp0.2 >=(400+12 × DCR) MPa, elongation percentage A >= (25-1.2 × DCR) %, wherein DCR is that secondary cold-rolling rolls lower rate, 5%≤DCR≤18%.
Beneficial effects of the present invention:
C content and Mn equivalent are improved in the alloying component of high-strength multi-phase Steels uncoated tinplate base of the present invention, with Ultra-low carbon Steel is compared, which saves steel-making vacuum decarburization technique, and steel-making cost reduces.
Compared with quick continuous annealing method, continuous annealing process annealing temperature control of the invention is more accurate and cooling Speed is lower, and the technique is low to equipment, operation control accuracy requirement, it is easier to plate form control and the wide specification uncoated tinplate base of production, It is more easily implemented extensive stable industrial production.
High-strength multi-phase Steels uncoated tinplate base of the present invention can carry out secondary cold-rolling to be facilitated compared to once cold rolling method Strip is further thinned；Compared to larger secondary cold-rolling rate obtain strip, the present invention obtain strip baking after be still able to maintain compared with High elongation percentage A >=(25-1.2 × DCR) %, DCR are that secondary cold-rolling rolls lower rate, 5%≤DCR≤18%.
Detailed description of the invention
Fig. 1 is the metallographic structure photo of 1 steel plate of the embodiment of the present invention.
Fig. 2 is that pearlite+martensite+cementite particle area topographies in 1 steel plate metallographic structure of the embodiment of the present invention shine Piece.
Specific embodiment
Below with reference to embodiment and attached drawing, the present invention will be further described.
Table 1 lists the alloying component of the embodiment of the present invention and comparative example, and table 2 illustrates the embodiment of the present invention and comparative example Main technique section feature and phase composition feature, table 3 be embodiment and comparative example baking after yield strength and elongation percentage performance (200 DEG C of baking temperature, baking time 30min.)
Embodiment 1
The alloying component of embodiment 1 is as shown in table 1: C:0.081%, Mn:0.5%, Al:0.05%, P:0.015%, N:0.005%, B:0.001%, Cr:0.02%, Cu:0.01%, Mo:0.001%.The phase composition feature and production work of the strip Skill is as shown in table 2: it is 10% that pearlite+martensite+cementite particle region, which accounts for volume fraction, and M-region accounts for volume fraction 2%, ferritic crystallite dimension be 6.5 μm, in martensite the solid solution capacity of C be 0.082%.The strip continuous annealing section temperature It is 720 DEG C, the soaking time of annealing section is 40s, and cooling velocity is 60 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 10%.Final 200 DEG C of strip, the mechanical property after 30min baking are as shown in table 3: yield strength Rp0.2 is 564MPa, fracture Elongation percentage 18%.
As seen from Figure 1, Figure 2, the present embodiment uncoated tinplate base tissue is by ferrite crystal grain, pearlite, martensite and cementite Particle composition, wherein it is 10% that pearlite+martensite+cementite particle region, which accounts for volume fraction, and M-region accounts for volume point Several 2%, ferritic crystallite dimension is 6.5 μm, and (ferrite grain size is upper scribing line in transverse direction in Fig. 1 metallographic structure Method measures), the solid solution capacity of C is 0.082% in martensite.
Embodiment 2
The alloying component of embodiment 2 are as follows: C:0.081%, Mn:0.5%, Al:0.05%, P:0.01%, N:0.005%, B:0.003%, Cr:0.05%, Ti:0.005%, Nb:0.2%, Cu:0.01%, Mo:0.005%.The phase composition of the strip is special Sign are as follows: it is 13% that pearlite+martensite+cementite particle region, which accounts for volume fraction, and M-region accounts for the 4% of volume fraction, Ferritic crystallite dimension is 6.5 μm, and the solid solution capacity of C is 0.095% in martensite.The strip continuous annealing section temperature is 750 DEG C, the soaking time of annealing section is 40s, and cooling velocity is 90 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 5%.Finally 200 DEG C of strip, the mechanical property after 30min baking: yield strength Rp0.2 is 512MPa, fracture elongation 20.9%.
Embodiment 3
The alloying component of embodiment 3 are as follows: C:0.135%, Mn:0.2%, Al:0.05%, P:0.01%, N:0.005%, B:0.003%, Cr:0.005%, Cu:0.03%, Mo:0.005%.The phase composition feature of the strip are as follows: pearlite+martensite+ It is 5% that cementite particle region, which accounts for volume fraction, and M-region accounts for the 1.2% of volume fraction, and ferritic crystallite dimension is 5.3 μm, the solid solution capacity of C is 0.071% in martensite.The strip continuous annealing section temperature is 705 DEG C, the soaking time of annealing section For 30s, cooling velocity is 50 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 5%.Final 200 DEG C of strip, 30min baking Mechanical property afterwards: yield strength Rp0.2 is 482MPa, fracture elongation 20.2%.
Embodiment 4
The alloying component of embodiment 4 are as follows: C:0.14%, Mn:0.5%, Al:0.01%, P:0.015%, N:0.015%, B:0.003%, Cr:0.02%, Ti:0.1%, Cu:0.01%, Mo:0.008%.The phase composition feature of the strip are as follows: pearlite It is 19% that+martensite+cementite particle region, which accounts for volume fraction, and M-region accounts for the 4.8% of volume fraction, ferritic crystalline substance Particle size is 6.2 μm, and the solid solution capacity of C is 0.1% in martensite.The strip continuous annealing section temperature is 800 DEG C, the guarantor of annealing section The warm time is 30s, and cooling velocity is 90 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 18%.Final 200 DEG C of strip, Mechanical property after 30min baking: yield strength Rp0.2 is 650MPa, fracture elongation 5.5%.
Embodiment 5
The alloying component of embodiment 5 are as follows: C:0.1%, Mn:0.8%, Al:0.035%, P:0.015%, N:0.015%, B:0.005%, Cr:0.02%, Ti:0.001%, Cu:0.01%.The phase composition feature of the strip are as follows: pearlite+martensite+ It is 14% that cementite particle region, which accounts for volume fraction, and M-region accounts for the 1.5% of volume fraction, and ferritic crystallite dimension is 6.8 μm, the solid solution capacity of C is 0.081% in martensite.The strip continuous annealing section temperature is 750 DEG C, the soaking time of annealing section For 50s, cooling velocity is 50 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 10%.Final 200 DEG C of strip, 30min baking Mechanical property afterwards: yield strength Rp0.2 is 544MPa, fracture elongation 15%.
Embodiment 6
The alloying component of embodiment 6 are as follows: C:0.1%, Mn:0.5%, Al:0.09%, P:0.03%, N:0.005%, B: 0.003%, Cr:0.02%, Ti:0.005%, Nb:0.001, Cu:0.005%.The phase composition feature of the strip are as follows: pearlite+ It is 5% that martensite+cementite particle region, which accounts for volume fraction, and M-region accounts for the 2.5% of volume fraction, ferritic crystal grain Having a size of 5.5 μm, the solid solution capacity of C is 0.09% in martensite.The strip continuous annealing section temperature is 700 DEG C, the guarantor of annealing section The warm time is 30s, and cooling velocity is 90 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 12%.Final 200 DEG C of strip, Mechanical property after 30min baking: yield strength Rp0.2 is 597MPa, fracture elongation 13%.
Embodiment 7
The alloying component of embodiment 7 are as follows: C:0.1%, Mn:0.5%, Al:0.09%, P:0.03%, N:0.002%, B: 0.003%, Cr:0.02%, Ti:0.005%, Cu:0.01%.The phase composition feature of the strip are as follows: pearlite+martensite+infiltration It is 14% that carbon body particle region, which accounts for volume fraction, and M-region accounts for the 3.5% of volume fraction, and ferritic crystallite dimension is 6.2 μm, the solid solution capacity of C is 0.089% in martensite.The strip continuous annealing section temperature is 750 DEG C, the soaking time of annealing section For 40s, cooling velocity is 80 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 10%.Final 200 DEG C of strip, 30min baking Mechanical property afterwards: yield strength Rp0.2 is 575MPa, fracture elongation 17%.
Embodiment 8
The alloying component of embodiment 8 are as follows: C:0.1%, Mn:0.5%, Al:0.05%, P:0.015%, N:0.005%, B: 0.003%, Cr:0.02%, Ti:0.005%, Cu:0.01%.The phase composition feature of the strip are as follows: pearlite+martensite+infiltration It is 19% that carbon body particle region, which accounts for volume fraction, and M-region accounts for the 1.2% of volume fraction, and ferritic crystallite dimension is 6.7 μm, the solid solution capacity of C is 0.080% in martensite.The strip continuous annealing section temperature is 800 DEG C, the soaking time of annealing section For 30s, cooling velocity is 50 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 5%.Final 200 DEG C of strip, 30min baking Mechanical property afterwards: yield strength Rp0.2 is 497MPa, fracture elongation 20.3%.
Comparative example 1
The alloying component of comparative example 1 are as follows: C:0.07%, Mn:0.5%, Al:0.09%, P:0.03%, N:0.002%, B: 0.003%, Cr:0.02%, Ti:0.005%, Cu:0.04%.The phase composition feature of the strip are as follows: without pearlite+martensitic regions Domain, ferritic crystallite dimension are 5.2 μm.The strip continuous annealing section temperature is 690 DEG C, and the soaking time of annealing section is 40s, Cooling velocity is 50 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 19%.Final 200 DEG C of strip, the power after 30min baking Learn performance: yield strength Rp0.2 is 645MPa, fracture elongation 0.5%.
Comparative example 2
The alloying component of comparative example 2 are as follows: C:0.1%, Mn:0.1%, Al:0.05%, P:0.008%, N:0.005%, B: 0.01%, Cr:0.02%, Ti:0.005%, Cu:0.01%.The phase composition feature of the strip are as follows: pearlite+martensite+carburizing It is 12% that body particle region, which accounts for volume fraction, and M-region accounts for the 3.2% of volume fraction, and ferritic crystallite dimension is 8.2 μ M, the solid solution capacity of C is 0.068% in martensite.The strip continuous annealing section temperature is 750 DEG C, and the soaking time of annealing section is 60s, cooling velocity is 50 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 10%.Final 200 DEG C of strip, after 30min baking Mechanical property: yield strength Rp0.2 be 501.3MPa, fracture elongation 8%.
Comparative example 3
The alloying component of comparative example 3 are as follows: C:0.1%, Mn:0.5%, Al:0.005%, P:0.05%, N:0.002%, B: 0.003%, Cr:0.02%, Ti:0.005%, Cu:0.01%, Mo:0.01%.The phase composition feature of the strip are as follows: pearlite+ It is 14% that martensite+cementite particle region, which accounts for volume fraction, and M-region accounts for the 7.8% of volume fraction, ferritic crystalline substance Particle size is 5.7 μm, and the solid solution capacity of C is 0.12% in martensite.The strip continuous annealing section temperature is 750 DEG C, annealing section Soaking time is 40s, and cooling velocity is 120 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 5%.Final 200 DEG C of strip, Mechanical property after 30min baking: yield strength Rp0.2 is 587MPa, fracture elongation 7.8%.
Comparative example 4
The alloying component of comparative example 4 are as follows: C:0.13%, Mn:0.5%, Al:0.05%, P:0.015%, N:0.005%, B:0.003%, Cr:0.02%, Ti:0.005%, Cu:0.01%.The phase composition feature of the strip are as follows: pearlite+martensite+ It is 21.6% that cementite particle region, which accounts for volume fraction, and M-region accounts for the 6.9% of volume fraction, ferritic crystallite dimension It is 8.4 μm, the solid solution capacity of C is 0.1% in martensite.The strip continuous annealing section temperature is 820 DEG C, the soaking time of annealing section For 40s, cooling velocity is 80 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 10%.Final 200 DEG C of strip, 30min baking Mechanical property afterwards: yield strength Rp0.2 is 555.8MPa, fracture elongation 10.2%.
Comparative example 5
The alloying component of comparative example 5 are as follows: C:0.10%, Mn:0.5%, Al:0.05%, P:0.015%, N:0.02%, B: 0.003%, Cr:0.10%, Ti:0.2%, Cu:0.01%.The phase composition feature of the strip are as follows: pearlite+martensite+carburizing It is 4% that body particle region, which accounts for volume fraction, and M-region accounts for the 0.6% of volume fraction, and ferritic crystallite dimension is 5.2 μ M, the solid solution capacity of C is 0.07% in martensite.The strip continuous annealing section temperature is 750 DEG C, and the soaking time of annealing section is 20s, cooling velocity is 80 DEG C/s when annealing, and strip secondary cold-rolling reduction ratio is 2%.Final 200 DEG C of strip, after 30min baking Mechanical property: yield strength Rp0.2 be 612.3MPa, fracture elongation 5.9%.
Comparative example 6
The alloying component of comparative example 6 are as follows: C:0.15%, Mn:0.9%, Al:0.05%, P:0.015%, N:0.01%, Cr:0.10%, Ti:0.2%, Nb:0.3%.The phase composition feature of the strip are as follows: it is 13% that perlitic range, which accounts for volume fraction, M-region accounts for the 0% of volume fraction, and ferritic crystallite dimension is 7.6 μm.The strip continuous annealing section temperature is 750 DEG C, the soaking time of annealing section is 40s, and cooling velocity is 30 DEG C/s, no secondary cold-rolling when annealing.Final 200 DEG C of strip, Mechanical property after 30min baking: yield strength Rp0.2 is 454.8MPa, fracture elongation 20.8%.

Claims (9)

1. a kind of high-strength multi-phase Steels uncoated tinplate base, chemical component mass percent are as follows: C:0.081~0.14%, Mn:0.2~ 0.8%, Al:0.01~0.09%, P:0.01~0.03%, N:0.002~0.015% also contain B:0.001~0.005%, Cr:0.005~0.05%, Ti:0.001~0.1%, Nb:0.001~0.2%, Cu:0.005~0.03%, Mo:0.001~ One or more kinds of in 0.008%, surplus is Fe and inevitable impurity；And following relationship need to be met simultaneously: 0.21%≤ Mn+1.3Cr+3.2Mo+0.5Cu≤0.91%.
2. high-strength multi-phase Steels uncoated tinplate base according to claim 1, which is characterized in that the high-strength multi-phase Steels uncoated tinplate base Tissue be made of ferrite crystal grain, pearlite, martensite and cementite particle.
3. high-strength multi-phase Steels uncoated tinplate base according to claim 1 or 2, which is characterized in that the high-strength multi-phase Steels are tin plating Ferrite grain size≤7 μm in the tissue of raw sheet.
4. high-strength multi-phase Steels uncoated tinplate base according to claim 2 or 3, which is characterized in that the high-strength multi-phase Steels are tin plating Tissue medium pearlite+martensite+cementite particle volume fraction of raw sheet is 5~20%.
5. high-strength multi-phase Steels uncoated tinplate base according to claim 2 or 4, which is characterized in that the high-strength multi-phase Steels are tin plating Martensite Volume Fraction is 1~5% in the tissue of raw sheet.
6. the high-strength multi-phase Steels uncoated tinplate base according to claim 2 or 4 or 5, which is characterized in that the high-strength multi-phase Steels plating Carbon solid solution capacity >=0.07% in martensite in tin raw sheet tissue.
7. high-strength multi-phase Steels uncoated tinplate base according to claim 1-6, which is characterized in that the high-strength multi-phase Steels After uncoated tinplate base baking, yield strength Rp0.2 >=(400+12 × DCR) MPa, elongation percentage A >=(25-1.2 × DCR) %, wherein DCR is that secondary cold-rolling rolls lower rate, 5%≤DCR≤18%.
8. such as the manufacturing method of the described in any item high-strength multi-phase Steels uncoated tinplate bases of claim 1-7, the change of the uncoated tinplate base Learn ingredient percent are as follows: C:0.081~0.14%, Mn:0.2~0.8%, Al:0.01~0.09%, P:0.01~ 0.03%, N:0.002~0.015%, also contain B:0.001~0.005%, Cr:0.005~0.05%, Ti:0.001~ 0.1%, Nb:0.001~0.2%, Cu:0.005~0.03%, one or more kinds of in Mo:0.001~0.008%, surplus For Fe and inevitable impurity, and following relationship: 0.21%≤Mn+1.3Cr+3.2Mo+0.5Cu≤0.91% need to be met simultaneously； The uncoated tinplate base is successively through continuous annealing, secondary cold-rolling, wherein continuous annealing section temperature T are as follows: (727-100 × C-30 × Mn- 1000 × N) DEG C≤T≤800 DEG C, soaking time is 30~50s, in 250 DEG C of temperatures above sections cooling velocity be 50~90 DEG C/ s；Secondary cold-rolling rolls lower rate DCR:5%≤DCR≤18%.
9. the manufacturing method of high-strength multi-phase Steels uncoated tinplate base according to claim 8, which is characterized in that the uncoated tinplate base Production stage before continuous annealing are as follows: smelting, hot rolling, pickling, once cold rolling.
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